EP2832882B1 - Tôle d'acier électromagnétique non orientée et procédé de production de cette dernière - Google Patents

Tôle d'acier électromagnétique non orientée et procédé de production de cette dernière Download PDF

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EP2832882B1
EP2832882B1 EP13768801.6A EP13768801A EP2832882B1 EP 2832882 B1 EP2832882 B1 EP 2832882B1 EP 13768801 A EP13768801 A EP 13768801A EP 2832882 B1 EP2832882 B1 EP 2832882B1
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steel sheet
sol
rolling
cold
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English (en)
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EP2832882A1 (fr
EP2832882A4 (fr
Inventor
Yoshiaki Natori
Kenichi Murakami
Takeaki Wakisaka
Hisashi Mogi
Takuya Matsumoto
Tomoji SHONO
Tatsuya Takase
Junichi TAKAOBUSHI
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Nippon Steel Corp
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Nippon Steel Corp
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    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F3/00—Cores, Yokes, or armatures
    • H01F3/02—Cores, Yokes, or armatures made from sheets
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/004—Very low carbon steels, i.e. having a carbon content of less than 0,01%
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1233—Cold rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1261—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest following hot rolling
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/001—Ferrous alloys, e.g. steel alloys containing N
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/008—Ferrous alloys, e.g. steel alloys containing tin
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/02—Ferrous alloys, e.g. steel alloys containing silicon
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/04—Ferrous alloys, e.g. steel alloys containing manganese
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/06—Ferrous alloys, e.g. steel alloys containing aluminium
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/08—Ferrous alloys, e.g. steel alloys containing nickel
    • C—CHEMISTRY; METALLURGY
    • C22—METALLURGY; FERROUS OR NON-FERROUS ALLOYS; TREATMENT OF ALLOYS OR NON-FERROUS METALS
    • C22C—ALLOYS
    • C22C38/00—Ferrous alloys, e.g. steel alloys
    • C22C38/14—Ferrous alloys, e.g. steel alloys containing titanium or zirconium
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/16—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/16—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets
    • H01F1/18—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys in the form of sheets with insulating coating
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F41/00—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties
    • H01F41/02—Apparatus or processes specially adapted for manufacturing or assembling magnets, inductances or transformers; Apparatus or processes specially adapted for manufacturing materials characterised by their magnetic properties for manufacturing cores, coils, or magnets
    • H01F41/0206—Manufacturing of magnetic cores by mechanical means
    • H01F41/0233—Manufacturing of magnetic circuits made from sheets
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D2211/00—Microstructure comprising significant phases
    • C21D2211/004—Dispersions; Precipitations
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1216—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the working step(s) being of interest
    • C21D8/1222—Hot rolling
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1266—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest between cold rolling steps
    • C—CHEMISTRY; METALLURGY
    • C21—METALLURGY OF IRON
    • C21D—MODIFYING THE PHYSICAL STRUCTURE OF FERROUS METALS; GENERAL DEVICES FOR HEAT TREATMENT OF FERROUS OR NON-FERROUS METALS OR ALLOYS; MAKING METAL MALLEABLE, e.g. BY DECARBURISATION OR TEMPERING
    • C21D8/00—Modifying the physical properties by deformation combined with, or followed by, heat treatment
    • C21D8/12—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties
    • C21D8/1244—Modifying the physical properties by deformation combined with, or followed by, heat treatment during manufacturing of articles with special electromagnetic properties the heat treatment(s) being of interest
    • C21D8/1272—Final recrystallisation annealing
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14766—Fe-Si based alloys
    • H01F1/14775—Fe-Si based alloys in the form of sheets
    • H—ELECTRICITY
    • H01—ELECTRIC ELEMENTS
    • H01F—MAGNETS; INDUCTANCES; TRANSFORMERS; SELECTION OF MATERIALS FOR THEIR MAGNETIC PROPERTIES
    • H01F1/00—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties
    • H01F1/01—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials
    • H01F1/03—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity
    • H01F1/12—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials
    • H01F1/14—Magnets or magnetic bodies characterised by the magnetic materials therefor; Selection of materials for their magnetic properties of inorganic materials characterised by their coercivity of soft-magnetic materials metals or alloys
    • H01F1/147—Alloys characterised by their composition
    • H01F1/14766—Fe-Si based alloys
    • H01F1/14791—Fe-Si-Al based alloys, e.g. Sendust
    • Y—GENERAL TAGGING OF NEW TECHNOLOGICAL DEVELOPMENTS; GENERAL TAGGING OF CROSS-SECTIONAL TECHNOLOGIES SPANNING OVER SEVERAL SECTIONS OF THE IPC; TECHNICAL SUBJECTS COVERED BY FORMER USPC CROSS-REFERENCE ART COLLECTIONS [XRACs] AND DIGESTS
    • Y10—TECHNICAL SUBJECTS COVERED BY FORMER USPC
    • Y10T—TECHNICAL SUBJECTS COVERED BY FORMER US CLASSIFICATION
    • Y10T29/00—Metal working
    • Y10T29/49—Method of mechanical manufacture
    • Y10T29/4998—Combined manufacture including applying or shaping of fluent material
    • Y10T29/49982—Coating
    • Y10T29/49986—Subsequent to metal working

Definitions

  • the present invention relates to a non-oriented electrical steel sheet used as an iron core of a motor for use mainly in, for example, an electric device and a hybrid vehicle, and a method of manufacturing the non-oriented electrical steel sheet.
  • the present application claims priority based on Japanese Patent Application No. 2012-075258 filed in Japan on March 29, 2012 .
  • the motors in these products have been miniaturized in response to the need for miniaturization and weight reduction, and further are designed to rotate at high speeds to meet the need for outputting sufficient power.
  • cores of the motors are required to be formed by a non-oriented electrical steel sheet having reduced high-frequency iron loss.
  • the iron loss can be reduced by increasing the resistivity of the non-oriented electrical steel sheet, as described, for example, in Patent Document 1.
  • alloying makes the steel sheet significantly brittle, which has a large adverse effect on the productivity.
  • Patent Document 1 the amount of Si + Al is controlled to be less than or equal to 4.5%. However, this control is not sufficient enough to prevent the steel sheet from becoming brittle. Further, Patent Document 1 does not take into consideration the effect of Mn, which is the main point of the present invention.
  • Patent Document 1 does not evaluate Bs, and hence, favorable magnetic property cannot be necessarily obtained.
  • Patent Document 2 describes making the relationship between resistivity and Bs constant. However, Patent Document 2 is not intended to obtain high torque, and cannot prevent the steel sheet from becoming brittle.
  • Patent Document 2 is not directed at improving iron loss at high frequencies, and does not take into consideration brittleness of a steel sheet having the amount of Si exceeding 3.0% or improvement in the iron loss of the steel sheet. Thus, favorable magnetic properties cannot be necessarily obtained.
  • JP 2008-127612 A deals with a non-oriented electromagnetic steel sheet.
  • JP H06-179914 describes the production of an ultrahigh silicon steel sheet with superior magnetic flux density.
  • Non-oriented electrical steel sheets are also disclosed in WO 2007/074987 .
  • the present invention is directed to solving the problems that the conventional arts described above have, and provides a non-oriented electrical steel sheet that has reduced iron loss, increased saturation magnetic flux density Bs, and exhibits excellent productivity, and a method of manufacturing the non-oriented electrical steel sheet. More specifically, the present invention provides a non-oriented electrical steel sheet with reduced high-frequency iron loss and increased Bs without causing deterioration in productivity, and a method of manufacturing the non-oriented electrical steel sheet.
  • the present invention it is possible to provide a non-oriented electrical steel sheet exhibiting reduced high-frequency iron loss and improved saturation magnetic flux density Bs while maintaining high productivity, and a method of manufacturing the non-oriented electrical steel sheet.
  • the present invention contributes to achieving highly efficient, high-performance motors for use in hybrid vehicles and electric vehicles in the field of automobiles, and in air conditioners and refrigerators in the field of household appliances, and further can maintain high productivity, which makes it possible to achieve reduced manufacturing costs.
  • FIG. 1 is a diagram illustrating an example of ranges of components according to the present invention.
  • the present inventors made a keen study on elements in a steel sheet and manufacturing conditions to solve the problems described above with regard to providing a non-oriented electrical steel sheet in line with the current tread of motors, in other words, achieving a non-oriented electrical steel sheet with magnetic properties having both sufficiently low high-frequency iron losses and high saturation magnetic flux density Bs in the case where the amount of Si is set to over 3.0%, while, from the viewpoint of manufacturing, the steel sheet maintains its toughness during manufacturing.
  • the present inventors revealed that it is possible to prevent deterioration in productivity while maintaining low high-frequency iron loss and high Bs by making the steel contain Si, sol.Al, and Mn in a well-balanced manner.
  • the present inventors revealed that the degree of brittleness can be evaluated by using Si + (2/3) ⁇ sol.Al + (1/5) ⁇ Mn, and further found that it is possible to alleviate the brittleness and reduce the risk of breakage during the time when the steel sheet is running, by setting this value to not more than 4.25.
  • the present inventors found that the risk of breakage during the time when the steel sheet is running can be effectively reduced by appropriately controlling temperatures of the steel sheet at the time of running the cold-drawn steel sheet, in addition to setting the chemical components in the range described above.
  • non-oriented electrical steel sheet hereinafter, also referred simply to as a steel sheet
  • a steel sheet according to an exemplary embodiment of the present invention that has been made on the basis of the findings described above
  • C causes magnetic aging, which leads to a deterioration in the magnetic properties, and it is desirable to minimize C as much as possible.
  • C is set to not more than 0.0040%.
  • the amount of C contained is preferably set to not more than 0.0030%, and more preferably set to not more than 0.0025%.
  • the lower limit of the amount of C contained is set to 0.0001%, and preferably to 0.0003%.
  • Si is an element that increases the resistivity of the electrical steel sheet and effectively reduces the iron loss. Further, Si has an economical advantage of increasing the resistivity at low cost. Thus, it is necessary for Si to exceed 3.0%.
  • the upper limit of the amount of Si contained is set to 3.7%, and preferably to 3.5%.
  • sol.Al is an element that increases the resistivity of the electrical steel sheet.
  • sol.Al greatly contributes to the reduction in Bs, and has a large effect on the brittleness of the steel sheet.
  • the upper limit of the amount of sol.Al contained is set to 1.0%, preferably to 0.9%, and more preferably to 0.8%.
  • the lower limit of the amount of sol.Al contained is set to 0.3%, preferably to 0.4%, and more preferably to 0.5%.
  • Mn is an element that increases resistivity of the electrical steel sheet without causing any serious deterioration in the brittleness of the steel sheet, and can effectively reduce the iron loss. Thus, Mn of 0.5% or more is necessary.
  • Mn causes the formation of austenite, and hence, if the amount of Mn is excessive, the phase is changed from a single phase formed only by ferrite during a high-temperature process in the manufacturing processing, which may significantly deteriorate the magnetic properties of the resulting sheet produced.
  • the upper limit of the amount of Mn contained is set to 1.5%, and preferably to 1.3%.
  • the resistivity at room temperature was obtained through a generally known four-terminal method.
  • the saturation magnetic flux density Bs at room temperature itself is an important magnetic property that contributes, for example, to motor torque.
  • the saturation magnetic flux density Bs at room temperature directly affects the magnetization process, and has an effect on the iron loss.
  • VSM vibrating sample magnetometer
  • Si, sol.Al, and Mn each represent values when contents in the steel sheet are expressed in terms of mass%.
  • the upper limit of Si + (2/3) ⁇ sol.Al + (1/5) ⁇ Mn is set preferably to 4.1, and more preferably to 4.0.
  • the resistivity at room temperature due to the necessity of setting the resistivity at room temperature to not less than 60 ⁇ cm, it is necessary to appropriately adjust the balance between the amounts of Si, sol.Al, and Mn added.
  • the value of Si + (2/3) ⁇ sol.Al + (1/5) ⁇ Mn is less than 3.5
  • the lower limit value of Si + (2/3) ⁇ sol.Al + (1/5) ⁇ Mn is set to 3.5, preferably to 3.6, and more preferably to 3.7.
  • Sn has an effect of improving texture after final-annealing to improve the B50 (magnetic flux density at the time of magnetization at 5000 A/m), and hence, the amount of Sn contained is set to not less than 0.005%, and preferably 0.01%.
  • the upper limit is set to 0.1%, preferably to 0.9%, and more preferably to 0.8%.
  • Ti precipitates in a form of, for example, TiN or TiC, which leads to a deterioration in magnetic properties and grain growth at the time of final-annealing.
  • the lower limit of the amount of Ti contained is set to 0.0001%, and preferably to 0.0003%.
  • S precipitates in a form of, for example, MnS, MgS, TiS, or CuS, which leads to a deterioration in magnetic properties and grain growth at the time of final-annealing. Thus, it is desirable to reduce S as much as possible.
  • the amount of S contained is set to not more than 0.0020% or less, and preferably to not more than 0.0015%.
  • the lower limit of the amount of S contained is set to 0.0001%, and preferably to 0.0003%.
  • N precipitates in a form of, for example, TiN or AlN, which leads to a deterioration in magnetic properties and grain growth at the time of final-annealing. Thus, it is desirable to reduce N as much as possible.
  • the amount of N contained is set to not more than 0.0030%, and preferably to 0.0025%.
  • the lower limit of the amount of N contained is set to 0.0001 %, and preferably to 0.0003%.
  • Ni has an effect of improving toughness of the steel sheet to reduce the risk of breakage during manufacturing.
  • Ni is set to not less than 0.001%.
  • Ni provides a higher effect with the increase in the amount of Ni added.
  • the upper limit of Ni is set to 0.2%.
  • P has an effect of improving texture after final-annealing to improve the B50, and hence, P is set to not less than 0.005%.
  • the upper limit is set to 0.05%, and preferably to 0.03%.
  • the chemical composition of the steel sheet described above contains Fe and impurities as the remainder other than the elements described above.
  • the remainder may only consist of Fe and impurities.
  • the impurities include, for example, O and B, which are inevitable impurities entering during manufacturing processes or other processes, and Cu, Cr, Ca, REM, and Sb, which are very small amounts of elements added for obtaining favorable magnetic properties. These impurities may be contained within a range that does not impair mechanical properties and magnetic properties of the present invention.
  • FIG. 1 An example of the ranges of components according to the present invention is illustrated in FIG. 1 .
  • a base steel formed by the components described above it may be possible to use a steel slab produced through melting in a converter and then a continuous casting or ingot-casting primary rolling process.
  • the steel slab is heated through a known method, and then is subjected to hot-rolling into a hot-rolled sheet having a required thickness.
  • the hot-rolled sheet is subjected to annealing or self-annealing as necessary.
  • This hot-rolled sheet is subjected to pickling, and then is cold-rolled once to form the sheet so as to have a predetermined thickness. Then, the sheet is subjected to final-annealing, and is insulation-coated.
  • the temperature needs to be set to not less than 50°C, and the resulting effect can be enhanced with the increase in the temperature.
  • the upper limit of the temperature is set to 200°C.
  • the rate at which the sheet runs is not more than 200 m/min, the effect of reducing the risk of breakage can be achieved.
  • the rate at which the sheet runs is excessively low, the effect of increasing the temperature of the steel sheet using the heat generated from working processes is significantly reduced, and the effect of reducing the risk of breakage resulting from the increase in the temperature of the steel sheet in the second pass or after is reduced.
  • the lower limit of the rate is set to 60 m/min.
  • the sheet is manufactured with a thickness of not more than 0.50 mm.
  • the thickness is set preferably to not less than 0.10 mm, and more preferably to not less than 0.20 mm.
  • Steel slabs containing various components shown in Table 1 adjusted appropriately in a manner such that the steel slabs had a resistivity ⁇ of approximately 60 ⁇ cm, with the balance including Fe and inevitable impurities, were prepared.
  • the steel slabs were hot-rolled so as to have a thickness of 2.0 mm, the sheets were subjected to hot-rolled-sheet annealing at 1000°C ⁇ 1 minute, pickling, and then cold-rolled so as to have a thickness of 0.30 mm.
  • the temperature of each of the sheets was set to 70°C, and the rate at which the sheets were run was set to 100 m/min.
  • the cold-rolled sheets were subjected to final-annealing at 1000°C ⁇ 15 seconds, and were insulation-coated.
  • the magnetism measurement was evaluated using an iron loss (W10/800) obtained at the time when sinusoidal magnetization was performed at a cycle of 800 Hz with the maximum magnetic flux density of 1.0T.
  • No. 1 to No. 4 had a resistivity of 60 ⁇ cm or lower, and as a result, the iron loss W10/800 exceeded 38 W/kg.
  • No. 5 to No. 12 had a resistivity of 60 ⁇ cm or higher.
  • No. 6 to No. 8 had an iron loss W10/800 exceeding 38W/kg, and had Bs lower than 1.970T, exhibiting poor magnetic properties.
  • No. 5 and No. 9 to No. 12 had an iron loss W10/800 less than or equal to 38W/kg, and had high Bs more than or equal to 1.970T, which resulted in excellent magnetic properties having a good balance between iron loss and Bs.
  • Steel slabs containing various components shown in Table 2 adjusted appropriately in a manner such that the steel slabs had a resistivity p at room temperature of approximately 65 ⁇ cm, with the balance including Fe and inevitable impurities, were prepared.
  • the steel slabs were hot-rolled so as to have a thickness of 2.0 mm, subjected to hot-rolled-sheet annealing at 1000°C ⁇ 1 minute, pickling, and then cold-rolled so as to have a thickness of 0.30 mm. Note that, in the first pass of the cold-rolling, the temperature of each of the sheets was set to 70°C, and the rate at which the sheets were run was set to 100 m/min.
  • the cold-rolled sheets were subjected to final-annealing at 1000°C ⁇ 15 seconds, and were insulation-coated.
  • the magnetism measurement was evaluated using an iron loss obtained at the time when sinusoidal magnetization was performed at a cycle of 800 Hz with the maximum magnetic flux density of 1.0T.
  • No. 13, No. 16, No. 17, No. 20, and No. 21 are examples of the present invention, and had a favorable iron loss lower than 37.0 W/kg as well as Bs exceeding 1.945T, which resulted in both excellent iron loss and Bs.
  • Steel slabs containing various components shown in Table 3 adjusted appropriately in a manner such that the steel slabs had a resistivity ⁇ at room temperature of approximately 69 ⁇ cm, with the balance including Fe and inevitable impurities, were prepared.
  • the steel slabs were hot-rolled so as to have a thickness of 2.0 mm, subjected to hot-rolled-sheet annealing at 1000°C ⁇ 1 minute, pickling, and then cold-rolled so as to have a thickness of 0.30 mm.
  • the temperature of each of the sheets was set to 70°C, and the rate at which the sheets were run was set to 100 m/min.
  • the cold-rolled sheets were subjected to final-annealing at 1000°C ⁇ 15 seconds, and were insulation-coated.
  • the magnetism measurement was evaluated using an iron loss obtained at the time when sinusoidal magnetization was performed at a cycle of 800 Hz with the maximum magnetic flux density of 1.0T.
  • No. 30 and No. 31 had significant brittleness, so that the samples were not able to be repaired after the breakage, and the sheet could not pass through.
  • No. 30 broke although having almost the same amounts of Si and sol.Al as those in No. 21 in Example 2. Thus, to prevent breakage, it is understood that it is important to make an evaluation by adding Mn and using Si + (2/3)sol.Al + (1/5)Mn.
  • No. 25, No. 26, No. 28, No. 29, No. 32, and No. 33 had an iron loss W10/800 exceeding 36.0 W/kg and Bs lower than 1.945T, which is a criterion of the present invention.
  • sol.Al fell outside the range of the present invention.
  • No. 23, No. 24, No. 27, and No. 34 are examples of the present invention, and had a favorable iron loss having W10/800 less than 36.0 W/kg, and having Bs exceeding 1.945T.
  • [Table 3] No. C Si sol.Al Mn Sn Ti S N Ni P Resistivity Bs W10/800 Si+(2/3)sol.Al +(1/5)Mn Breakage Note (ppm) (mass%) (mass%) (mass%) (mass%) (mass%) (mass%) (mass%) (mass%) (ppm) (ppm) (ppm) (mass%) (mass%) ⁇ cm (T) (W/kg) 23 14 3.40 0.70 1.48 0.010 16 8 12 0.12 0.012 69.0 1.964 35.86 4.16 No Example of the present invention 24 13 3.55 0.61 1.34 0.045 13 11 10 0.10 0.010 69.0 1.948 35.74 4.22 No Example of the present invention 25 15 3.20 1.12 1.25 0.010 11
  • the cold-rolled sheets were subjected to final-annealing at 1000°C ⁇ 15 seconds, and were insulation-coated.
  • No. 36 passed through the first pass at a slow rate. Hence, temperatures of the coils were reduced in the second pass, and breakage occurred during the cold-rolling.
  • No. 41 passed through at a rate faster than the range of the present invention, and breakage occurred during the cold-rolling. Further, the shape of the cold-rolled sheet was poor, and breakage occurred in the following final-annealing.
  • No. 42 and No. 43 passed through the first pass at temperatures lower than the range of the present invention, and breakage occurred in the first pass during rolling. Further, a large number of small cracks were found on the end surface of the coil in the width direction, and breakage occurred in the following final-annealing.
  • Steel slabs containing various components shown in Table 5 adjusted appropriately in a manner such that the steel slabs had a resistivity ⁇ at room temperature of approximately 69 ⁇ cm, with the balance including Fe and inevitable impurities, were prepared.
  • the steel slabs were hot-rolled so as to have a thickness of 2.0 mm, the hot-rolled sheets were subjected to pickling without application of hot-rolled-sheet annealing, and then cold-rolled so as to have a thickness of 0.30 mm.
  • the temperature of each of the sheets was set to 70°C, and the rate at which the sheets were run was set to 100 m/min.
  • the cold-rolled sheets were subjected to final-annealing with 1050°C ⁇ 15 seconds, and were insulation-coated.
  • the magnetism measurement was evaluated using an iron loss obtained at the time when sinusoidal magnetization was performed at a cycle of 800 Hz with the maximum magnetic flux density of 1.0T.
  • the iron loss W10/800 was higher than that of No. 23 to No. 35 that had the hot-rolled-sheet annealing applied thereto, although temperatures during final-annealing were increased to 1050°C.
  • No. 49 had an iron loss W10/800 higher than 37.0 W/kg and Bs lower than 1.945T, which is a criterion of the present invention.
  • sol.Al fell outside the range of the present invention.
  • No. 47 and No. 48 are examples of the present invention and had a favorable iron loss having W10/800 less than 37.0 W/kg and having Bs more than or equal to 1.945T.
  • the present invention it is possible to provide a non-oriented electrical steel sheet having reduced iron loss and increased saturation magnetic flux density Bs, and exhibiting excellent productivity, and a method of manufacturing the non-oriented electrical steel sheet.

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  • Metallurgy (AREA)
  • Organic Chemistry (AREA)
  • Physics & Mathematics (AREA)
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  • Manufacturing & Machinery (AREA)
  • Electromagnetism (AREA)
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  • Crystallography & Structural Chemistry (AREA)
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Claims (3)

  1. Tôle d'acier électrique non-orienté, consistant en, en % en masse :
    C : au moins 0,0001 % et au plus 0,0040 %,
    Si : plus de 3,0 % et au plus 3,7 %,
    Al sol. : au moins 0,3 % et au plus 1,0 %,
    Mn : au moins 0,5 % et au plus 1,5 %,
    Sn : au moins 0,005 % et au plus 0,1 %,
    Ti : au moins 0,0001 % et au plus 0,0030 %,
    S : au moins 0,0001 % et au plus 0,0020 %,
    N : au moins 0,0001 % et au plus 0,003 %,
    Ni : au moins 0,001 % et au plus 0,2 %, et
    P : au moins 0,005 % et au plus 0,05 %,
    avec un reste consistant en Fe et impuretés, dans laquelle
    une résistivité ρ à température ambiante ≥ 60 µΩcm, et une densité de flux magnétique de saturation Bs à température ambiante ≥ 1,945T sont établies, et
    les constituants contenus satisfont 3,5 ≤ Si + (2/3) x Al sol. + (1/5) x Mn ≤ 4,25.
  2. Tôle d'acier électrique non-orienté selon la revendication 1, dans laquelle :
    la quantité de Mn n'est pas inférieure à 0,7 % en % en masse ;
    la quantité de Al sol. est inférieure à celle de Mn ; et
    les constituants contenus satisfont 3,7 ≤ Si + (2/3) x Al sol. + (1/5) x Mn ≤ 4,0.
  3. Procédé de fabrication de la tôle d'acier électrique non-orienté selon la revendication 1 ou 2, incluant :
    le laminage à chaud d'une plaque contenant les constituants chimiques spécifiés dans la revendication 1 ou 2 ;
    après le laminage à chaud, l'application de recuit ou d'auto-recuit de tôle laminée à chaud, ou sans application du recuit de tôle laminée à chaud, et l'application d'un décapage dans chaque cas ;
    l'application d'un laminage à froid une fois ; et
    après le laminage à froid, l'application de recuit final, et l'application de revêtement, dans lequel
    pendant le laminage à froid, la température d'une tôle d'acier lorsque le laminage à froid démarre est fixée à pas moins de 50°C ni plus de 200°C, et une vitesse à laquelle la tôle d'acier passe à travers un premier passage pendant le laminage est fixée à pas moins de 60 m/min ni plus de 200 m/min.
EP13768801.6A 2012-03-29 2013-03-27 Tôle d'acier électromagnétique non orientée et procédé de production de cette dernière Active EP2832882B1 (fr)

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JPWO2013146879A1 (ja) 2015-12-14
KR101974674B1 (ko) 2019-05-03
KR102041897B1 (ko) 2019-11-08
PL2832882T3 (pl) 2020-02-28
JP5935834B2 (ja) 2016-06-15
KR20160136462A (ko) 2016-11-29
JP5644959B2 (ja) 2014-12-24
KR20180051672A (ko) 2018-05-16
CN103842544A (zh) 2014-06-04
KR102012610B1 (ko) 2019-08-20
US9570219B2 (en) 2017-02-14
KR20140050743A (ko) 2014-04-29
CN103842544B (zh) 2016-10-12
JP2014210978A (ja) 2014-11-13
WO2013146879A1 (fr) 2013-10-03
US20140227127A1 (en) 2014-08-14
EP2832882A1 (fr) 2015-02-04
EP2832882A4 (fr) 2015-12-16

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